CN113168961A - Method for manufacturing rare earth magnet - Google Patents
Method for manufacturing rare earth magnet Download PDFInfo
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- CN113168961A CN113168961A CN201980078204.8A CN201980078204A CN113168961A CN 113168961 A CN113168961 A CN 113168961A CN 201980078204 A CN201980078204 A CN 201980078204A CN 113168961 A CN113168961 A CN 113168961A
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Images
Classifications
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
- H01F41/0293—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets diffusion of rare earth elements, e.g. Tb, Dy or Ho, into permanent magnets
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
- H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
- H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
- H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2202/00—Physical properties
- C22C2202/02—Magnetic
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- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Hard Magnetic Materials (AREA)
- Powder Metallurgy (AREA)
- Manufacturing Cores, Coils, And Magnets (AREA)
Abstract
Embodiments disclose a method of manufacturing a rare earth magnet, the method including the steps of: preparing a magnet sintered body containing RE, Fe, and B as components (RE is at least one selected from rare earth elements); coating the sintered body with a solution containing a grain boundary diffusion material; and heat-treating the sintered body to perform grain boundary diffusion of the sintered body, wherein the grain boundary diffusion material contains a Heavy Rare Earth Element (HREE) hydride and a Light Rare Earth Element (LREE) hydride.
Description
Technical Field
The present invention relates to a method of manufacturing a rare earth magnet.
Background
In general, since sintered permanent magnets are poor in reliability at high temperatures, a high coercive force is required for use as a traction motor or an EPS motor. In order to secure high coercive force, a permanent magnet may be manufactured by adding heavy rare earth elements such as Dy and Tb.
At present, the most common method is to use a composite alloy in which a part of Nd is substituted with Dy or Tb. Make Nd2Fe14Substitution of Nd in the B compound by these elements increases both the anisotropic magnetic field and the coercive force of the compound. However, substitution by Dy or Tb reduces the saturation magnetic polarization of the compound. Therefore, when only the coercive force is increased by the above method, there is a problem that the residual magnetic flux density is lowered.
In an Nd-Fe-B magnet, the coercive force is the magnitude of an external magnetic field of a core that generates a reverse magnetic domain at a grain boundary. The nucleation of the reverse magnetic domain is strongly influenced by the structure of the grain boundaries, and disorder of the crystal structure near the boundaries causes disorder of the magnetic structure and promotes the generation of the reverse magnetic domain. In general, it is considered that the magnetic structure extending from the grain boundary to a depth of about 5nm contributes to the increase of the coercive force.
At the same time, by making traces of Dy or only in the vicinity of grain boundariesTb diffuses to increase the anisotropic magnetic field only in the vicinity of the boundary, the coercive force can be increased while suppressing the decrease in the residual magnetic flux density, and there is a manufacturing method of: which comprises separately producing Nd2Fe14A B compound composite alloy and a Dy-or Tb-rich alloy, mixing them, and then sintering the mixture. In this method, Dy or Tb-rich alloy becomes liquid phase during sintering and disperses to surround Nd2Fe14And (B) a compound.
Therefore, substitution of Nd by Dy or Tb occurs only in the vicinity of the grain boundary in the compound, so that the coercive force can be effectively increased while suppressing a decrease in residual magnetic flux density. However, this method also has a problem of an increase in manufacturing cost due to the use of expensive Dy or Tb.
Disclosure of Invention
Technical problem
The present invention aims to provide a method for manufacturing a rare earth magnet, which can reduce the use amount of heavy rare earth.
The problem to be solved in the embodiments is not limited thereto, and also includes objects and effects that can be grasped from the solutions or embodiments of the problems described below.
Technical scheme
An aspect of the present invention is to provide a method of manufacturing a rare earth magnet, the method including: preparing a magnetic sintered body containing RE, Fe and B as constituent components (RE is selected from one or two or more selected from rare earth elements); applying a solution containing a grain boundary diffusion material to the sintered body; and performing grain boundary diffusion by heat-treating the sintered body, wherein the grain boundary diffusion material contains a Heavy Rare Earth Element (HREE) hydride and a Light Rare Earth Element (LREE) hydride.
The Heavy Rare Earth Element (HREE) hydride may include at least one of Dy hydride, Tb hydride, and Ho hydride.
The Light Rare Earth Element (LREE) hydride may include Nd hydride (NdHx).
The amount of Heavy Rare Earth Element (HREE) hydride may be less than the amount of Light Rare Earth Element (LREE) hydride.
The amount of Heavy Rare Earth Element (HREE) hydride may be greater than the amount of Light Rare Earth Element (LREE) hydride.
Another aspect of the present invention provides a method of manufacturing a rare earth magnet, the method including: preparing a magnetic sintered body containing RE, Fe and B as constituent components (RE is selected from one or two or more selected from rare earth elements); applying a first solution containing a first grain boundary diffusion material to the sintered body; performing first grain boundary diffusion by heat-treating the sintered body; applying a second solution comprising a second grain boundary diffusion material to the sintered body; and performing second grain boundary diffusion by heat-treating the sintered body.
The first grain boundary diffusion material may include a Heavy Rare Earth Element (HREE) hydride, and the second grain boundary diffusion material may include a Light Rare Earth Element (LREE) hydride.
Advantageous effects
According to an embodiment, since the amount of heavy rare earth used can be reduced, the manufacturing cost can be reduced. Further, a decrease in coercive force and magnetic flux density can be prevented.
Various advantageous advantages and effects of the present invention are not limited to the above description and will be more easily understood in describing specific embodiments of the present invention.
Drawings
Figure 1 is a conceptual diagram of a motor according to one embodiment of the present invention,
figure 2 is a conceptual diagram of a magnet according to one embodiment of the invention,
figure 3 is an enlarged view of a conventional sintered magnet,
figure 4 is an enlarged view of the diffusion magnet,
figure 5 is a conceptual diagram of a magnet according to another embodiment of the present invention,
FIG. 6 shows the results of Electron Probe Microanalyzer (EPMA) analysis showing the amount of rare earth in a magnet according to one embodiment of the present invention,
figure 7 shows the results of EPMA analysis showing the amount of rare earth in a magnet according to another embodiment of the present invention,
fig. 8 is a flowchart for describing a method of manufacturing a rare earth magnet according to an embodiment of the present invention,
fig. 9 is a flowchart for describing a method of manufacturing a rare earth magnet according to another embodiment of the present invention,
FIG. 10 is a graph of the change in remanence (Br) according to the coating amount, an
Fig. 11 is a graph of the change in coercive force (Hcj) according to the coating amount.
Detailed Description
Hereinafter, exemplary embodiments of the present invention will be described in detail with reference to the accompanying drawings.
However, the technical spirit of the present invention is not limited to some embodiments to be described, but may be implemented in various different forms, and one or more of the constituent elements in the embodiments may be selectively combined or substituted within the scope of the technical spirit of the present invention.
Further, unless explicitly defined and explained, terms (including technical and scientific terms) used in embodiments of the present invention may be interpreted in a meaning that is commonly understood by those skilled in the art to which the present invention belongs, and a meaning of a commonly used term (e.g., a term defined in a dictionary) may be interpreted in consideration of a meaning in the context of the related art.
Furthermore, the terminology used in the embodiments of the present invention is for the purpose of describing the embodiments and is not intended to be limiting of the invention.
In this specification, unless explicitly stated in the phrase, the singular form may include the plural form, and at least one (or one or more) of "A, B and C" may include one or more of all possible combinations of A, B and C.
In describing the constituent elements according to the embodiments of the present invention, terms such as first, second, "a", "B", "a), (B), and the like may be used.
These terms are only intended to distinguish one constituent element from another constituent element, and do not limit the nature, order, or sequence of the constituent elements.
Further, it should be noted that when one constituent element is described as being "connected", "coupled", or "joined" to another constituent element in the specification, the former may be directly "connected", "coupled", and "joined" to the latter or may be "connected", "coupled", and "joined" to the latter through another constituent element.
Further, it will be understood that, when each constituent element is referred to as being formed or arranged "on (above)" or "under (below)" another constituent element, it may be directly "on" or "under" the other constituent element or one or more additional constituent elements interposed therebetween may be indirectly formed. Further, it will also be understood that when each constituent element is referred to as being formed or arranged "on (above)" or "under (below)" another constituent element, it may mean an upward direction and a downward direction based on one constituent element.
Fig. 1 is a conceptual diagram of a motor according to an embodiment of the present invention, fig. 2 is a conceptual diagram of a magnet according to an embodiment of the present invention, fig. 3 is an enlarged view of a conventional sintered magnet, and fig. 4 is an enlarged view of a diffusion magnet.
Referring to fig. 1, the motor may include a housing 110, a stator 130, a rotor 120, and a rotation shaft 140. The housing 110 may include a space for accommodating the stator 130 and the rotor 120. The material and structure of the housing 110 are not particularly limited. The motor of an embodiment may be an assembly having components positioned in the housing 110, or may be a combination having various components (stator and rotor) positioned in the upper system.
The housing 110 may further include a cooling structure (not shown) to easily remove internal heat. The cooling structure may be an air cooling structure or a water cooling structure, but is not limited thereto.
The stator 130 may be positioned in the inner space of the housing 110. The stator 130 may include a stator core and a coil. The stator core may include a plurality of divided cores coupled in the axial direction, but is not necessarily limited thereto.
The rotor 120 may be positioned to be rotatable with respect to the stator 130. The rotor 120 may include a plurality of magnets 121 positioned on an outer circumferential surface of the rotor core. However, the magnet 121 may be inserted and positioned in the rotor core 210.
The rotation shaft 140 may be coupled to a central portion of the rotor 120. Accordingly, the rotor 120 and the rotation shaft 140 may rotate together. The rotation shaft 140 may be supported by a first bearing 151 positioned at one side thereof and a second bearing 152 positioned at the other side thereof.
The motor may be a traction motor or an EPS motor, but is not necessarily limited thereto and may be applied to various types of motors. Further, the magnet according to one embodiment may be applied to various apparatuses in which the magnet is mounted in addition to the motor.
Referring to fig. 2, the magnet may include a crystal structure 121a of a magnetic sintered body containing RE, Fe, and B as constituent components, and a diffusion layer 121B diffused at a grain boundary of the crystal structure 121 a. Further, a Nd-rich region 121c may be formed between the crystal 121a and the crystal 121 a. The Nd-rich region 121c may be defined as a region in which the composition of Nd is relatively higher than other compositions.
The magnetic sintered body can be produced by using a rare earth magnet powder containing RE, Fe, and B as constituent components. Here, RE may be selected from one or two or more of one or more rare earth elements from Nd, Pr, La, Ce, Ho, Dy and Tb. Hereinafter, the rare earth magnet powder is described as a Nd — Fe-B based sintered magnet, but the type of magnet powder is not necessarily limited thereto.
The diffusion layer 121b may include a Heavy Rare Earth Element (HREE) and a Light Rare Earth Element (LREE). The heavy rare earth may include at least one of Pm, Sm, Eu, Gd, Dy, Tb, and Ho. Further, the light rare earth may include at least one of La, Ce, Pr, and Nd. For example, the composition of the diffusion layer 121b may include the composition of Dy/Nd, Tb/Nd, Ho/Nd, Dy/Pr, Dy/Ho/Nd, Dy/Ho/Pr, and the like.
According to one embodiment, light rare earth (Ho, Nd) having a relatively low price may be used instead of heavy rare earth (Dy, Tb) having a relatively high price. Therefore, there is an advantage that the amount of heavy rare earth (Dy, Tb) used is reduced, thereby reducing the manufacturing cost.
However, the present invention is not necessarily limited thereto, and the diffusion layer 121b may be composed of only heavy rare earth or may be composed of only light rare earth. For example, the diffusion layer 121b may be composed of Dy/Tb, Tb/Ho, Dy/Tb/Ho, and Pr/Nd.
The diffusion layer 121b may be formed by wet coating a rare earth element powder on a base magnet as a sintered permanent magnet, and then performing diffusion at a high temperature. That is, when the permanent magnet coated with the rare earth element powder is heat-treated at high temperature, some of the rare earth element diffuses through the grain boundary of the magnet, thereby forming a core-shell structure. That is, the diffusion layer 121b may be defined as a shell. Referring to fig. 3 and 4, a general sintered magnet and a diffusion magnet in which a rare earth element is diffused may be distinguished from each other in a BSE SEM image.
Fig. 5 is a conceptual diagram of a magnet according to another embodiment of the present invention, fig. 6 is an Electron Probe Microanalyzer (EPMA) analysis result showing an amount of rare earth in the magnet according to one embodiment of the present invention, and fig. 7 is an EPMA analysis result showing an amount of rare earth in the magnet according to another embodiment of the present invention.
Even when a plurality of rare earths are mixed, the diffusion layer 121b may form a single layer. However, as shown in fig. 5, the diffusion layer 121b may be divided into a plurality of layers. For example, the inner layer 121b-1 may be composed of an element having a relatively high diffusion rate, and the outer layer 121b-2 may be composed of an element having a relatively low diffusion rate. For example, when Dy and Ho are mixed, applied to a magnet, and then subjected to heat treatment, Dy that diffuses quickly may be formed in the inner portion, and Ho that diffuses slowly may be formed in the outer layer.
As a result of the EPMA analysis, Dy and Ho were detected at the same position in the crystal as shown in fig. 6, thereby forming a monolayer. However, as shown in fig. 7, Dy is located on the inner side of Ho, thereby forming a plurality of layers. According to one embodiment, a plurality of layers may be intentionally formed, except for the case where layering is performed by diffusion rate. For example, when the respective rare earth element powders are subjected to the separate coating process and the heat treatment process, the diffusion layer 121b may be divided into a plurality of layers.
In addition to EPMA, the detection position and the detection amount of the diffusion element can be finally determined by Transmission Electron Microscopy (TEM), Electron Back Scattering Diffraction (EBSD) analysis, and Secondary Ion Mass Spectrometry (SIMS). In this case, the initial coating amount and the detection amount before diffusion may be changed according to the degree of diffusion and the diffusion position after diffusion.
Fig. 8 is a flowchart for describing a method of manufacturing a rare earth magnet according to an embodiment of the present invention.
Referring to fig. 8, a method of manufacturing a rare earth magnet according to an embodiment of the present invention includes: step S11 of preparing a magnetic sintered body containing RE, Fe, and B as constituent components; a step S12 of applying a solution containing a grain boundary diffusion material to the sintered body; and a step S13 of performing grain boundary diffusion by heat treatment of the sintered body.
In step S11 of preparing the magnetic sintered body containing RE, Fe, and B as constituent components, first, a rare earth magnet powder containing an RE-B-TM-Fe constituent component may be used. Here, RE may be a rare earth element, and TM may be a 3d transition element. Although not necessarily limited thereto, the amount of RE may be 28 to 35 parts by weight, the amount of B may be 0.5 to 1.5 parts by weight, and the amount of TM may be 0 to 15 parts by weight, based on 100 parts by weight of the total weight of the rare earth magnet powder. Further, Fe may be contained as the balance.
In one embodiment, an alloy of the composition may be melted by a vacuum induction heating method and manufactured into an alloy ingot by using a strip casting method. In order to improve the pulverization ability of these alloy ingots, hydrotreating and dehydrogenation are performed at a temperature range of room temperature to 600 ℃, and then, these alloy ingots may be manufactured into uniform and fine powders having a particle size of 1 μm to 10 μm by using pulverization methods such as jet milling, airy tower milling (atrita milling), ball milling, and vibration milling.
The process of manufacturing 1 to 10 μm powder from the alloy ingot is preferably performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
After that, the profiling in a magnetic field can be performed by using fine powder. For example, a mold is filled with ground powder, and the ground powder is oriented by applying a direct-current magnetic field by electromagnets positioned on the left and right of the mold, and at the same time, compression molding is performed by upper and lower punches, thereby manufacturing a molded body. The pressing in the magnetic field may be performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination with oxygen.
When the profiling in the magnetic field is completed, the molded body can be sintered. Although the sintering conditions are not limited, the sintering may be performed at a temperature in the range of 900 ℃ to 1100 ℃, and the heating rate at 700 ℃ or higher may be adjusted in the range of 0.5 ℃/min to 15 ℃/min.
For example, a molded body obtained by press molding in a magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 ℃ or less, thereby completely removing residual impure organic materials. Thereafter, the temperature is raised to be in the range of 900 to 1100 ℃ and maintained for 1 to 4 hours to perform a sintering densification process.
The sintering atmosphere is preferably an inert gas atmosphere such as vacuum and argon, and the heating rate may be adjusted to 0.1 to 10 deg.c/min, preferably 0.5 to 15 deg.c/min, at a temperature of 700 deg.c or higher.
Optionally, the sintered body after sintering may be stabilized by being subjected to post heat treatment in the range of 400 ℃ to 900 ℃ for 1 hour to 4 hours, and then processed into a predetermined size, thereby producing a rare earth magnetic sintered body.
In the step S12 of applying a solution, a solution containing a grain boundary diffusion material may be applied to the manufactured magnet. The grain boundary diffusion material may include a Heavy Rare Earth Element (HREE) hydride and a Light Rare Earth Element (LREE) hydride. According to one embodiment, there is an advantage of reducing manufacturing costs by diffusing a large amount of light rare earth having a relatively low price.
The Heavy Rare Earth Element (HREE) hydride may include at least one of Dy hydride, Tb hydride, and Ho hydride, and the Light Rare Earth Element (LREE) hydride may include Nd hydride (NdHx). At this time, the amount of the Heavy Rare Earth Element (HREE) hydride in parts by weight may be less than that of the Light Rare Earth Element (LREE) hydride in parts by weight based on 100 parts by weight of the grain boundary diffusion material. Therefore, there is an advantage in that the manufacturing cost is further reduced by increasing the weight of the light rare earth having a relatively low price in the diffusion process. However, the present invention is not necessarily limited thereto, and the amount of the Heavy Rare Earth Element (HREE) hydride in parts by weight may be greater than or equal to the amount of the Light Rare Earth Element (LREE) hydride in parts by weight in consideration of the limitation of diffusion.
In detail, any one of Ho hydride, Dy hydride, and Tb hydride may be mixed with at least one of light rare earth element hydrides to prepare a grain boundary diffusion material, and the grain boundary diffusion material and alcohol may be uniformly mixed at a ratio of 50%: 50% to prepare a rare earth compound slurry. While the prepared slurry was put into a beaker and uniformly dispersed using an ultrasonic cleaner, the treated body was immersed therein, and then the solution could be uniformly applied to the surface of the magnet.
In the step S13 of performing grain boundary diffusion, in order to diffuse the applied Heavy Rare Earth Element (HREE) hydride and Light Rare Earth Element (LREE) hydride into the grain boundaries in the magnet, the sintered magnet coated with the solution may be loaded into a heating furnace, heated so that the heating rate in an argon atmosphere is 0.1 to 10 ℃/min, and thus maintained at a temperature of 700 to 1000 ℃ for 4 to 8 hours. In this process, the heavy rare earth element hydride is decomposed into heavy rare earth, and the light rare earth element hydride is decomposed into light rare earth, the heavy rare earth element hydride and the light rare earth element hydride diffuse into the inside of the magnet, and a permeation reaction can be performed.
At this time, in order to prevent the generation of residual stress inside the magnet due to rapid diffusion, a step of removing stress by performing heat treatment in the range of 400 ℃ to 1000 ℃ after the completion of the diffusion reaction may be further included.
Fig. 9 is a flowchart for describing a method of manufacturing a rare earth magnet according to another embodiment of the present invention.
Referring to fig. 9, a method of manufacturing a rare earth magnet according to another embodiment of the present invention includes: step S21 of preparing a magnetic sintered body containing RE, Fe, and B as constituent components; a step S22 of applying a first solution containing a first grain boundary diffusion material to the sintered body; a step S23 of performing first grain boundary diffusion by heat-treating the sintered body; a step S24 of applying a second solution containing a second crystal boundary diffusion material to the sintered body; and a step S25 of performing second crystal boundary diffusion by heat treatment of the sintered body.
The step S21 of preparing the magnetic sintered body may be the same as the above-described step S11.
In the step S22 of applying the first solution, the first grain boundary diffusion material composed of the heavy rare earth element hydride and/or the light rare earth element hydride and the alcohol may be adjusted to a ratio of 50%: 50%, and then uniformly mixed to prepare the rare earth compound slurry. Thereafter, the treated body was immersed therein and maintained for 1 to 2 minutes while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, so that the slurry could be uniformly applied to the surface of the magnet.
In the step S23 of performing the first grain boundary diffusion, in order to diffuse the applied rare earth compound into the grain boundaries in the magnet, the solution-coated sintered magnet may be loaded into a heating furnace, heated in an argon atmosphere, and then held at a temperature of 700 to 1000 ℃ for 4 to 8 hours. In this process, the rare earth compound is decomposed into rare earth and then diffused into the inside of the magnet, so that a permeation reaction can be performed.
After the diffusion treatment, the diffusion layer is removed from the surface, and then a stress relief heat treatment may be performed at a temperature of 400 ℃ to 1000 ℃.
In the step S24 of applying the second solution, the second crystal boundary diffusion material composed of the heavy rare earth element hydride and/or the light rare earth element hydride and the alcohol may be adjusted to a ratio of 50%: 50%, and then uniformly mixed to prepare the rare earth compound slurry. Thereafter, while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the treated body was immersed therein and maintained for 1 to 2 minutes, so that the slurry could be uniformly applied to the surface of the magnet.
At this time, the first grain boundary diffusion material may be different from the second grain boundary diffusion material. For example, the first grain boundary diffusion material may be a hydride of a heavy rare earth element, and the second grain boundary diffusion material may be a hydride of a light rare earth element. Conversely, the first grain boundary diffusion material may be a hydride of a light rare earth element and the second grain boundary diffusion material may be a hydride of a heavy rare earth element.
The coating amount of the first grain boundary diffusion material may be different from the coating amount of the second grain boundary diffusion material. For example, the amount of the first grain boundary diffusion material (heavy rare earth element hydride) may be 0.1 to 1.0 parts by weight based on 100 parts by weight of the total weight of the magnet, and the amount of the second grain boundary diffusion material (light rare earth element hydride) may be 0.1 to 0.5 parts by weight based on 100 parts by weight of the total weight of the magnet. Conversely, the amount of the first grain boundary diffusion material (heavy rare earth element hydride) may be 0.1 to 0.5 parts by weight based on 100 parts by weight of the total weight of the magnet, and the amount of the second grain boundary diffusion material (light rare earth element hydride) may be 0.1 to 1.0 parts by weight based on 100 parts by weight of the total weight of the magnet.
In the step S25 of performing the second grain boundary diffusion, in order to diffuse the applied rare earth compound into the grain boundaries in the magnet, the applied body may be charged into a heating furnace, heated in an argon atmosphere, and then held at a temperature of about 700 ℃ to about 1000 ℃ for 4 hours to 8 hours. In this process, the rare earth compound is decomposed into rare earth and then diffused into the inside of the magnet, so that a permeation reaction can be performed.
After the diffusion treatment, the diffusion layer is removed from the surface, and then a stress relief heat treatment may be performed at a temperature of 400 ℃ to 1000 ℃.
According to one embodiment, the diffusion efficiency of the rare earth in the grain boundary may be increased by the first diffusion and the second diffusion. Therefore, the coercive force and/or residual magnetic flux density can be increased as compared with the case where only the first diffusion is performed.
Hereinafter, it will be described in more detail by the following examples.
[ example 1]
An alloy consisting of X wt% RE-Y wt% B-Z wt% TM-the balance wt% Fe (where RE ═ rare earth element, TM ═ 3d transition element, X ═ 28 to 35, Y ═ 0.5 to 1.5, and Z ═ 0 to 15) was melted in an argon atmosphere by an induction heating method, and then rapidly cooled using a strip casting method, thereby producing an alloy strip.
In the course of coarsely pulverizing the produced alloy strip, the strip is charged into a vacuum furnace, evacuated, and then maintained in a hydrogen atmosphere for at least 2 hours so that hydrogen is absorbed into the strip. Subsequently, the strip was heated to 600 ℃ in a vacuum atmosphere, thereby removing hydrogen present in the interior of the strip. The coarsely pulverized and hydrotreated powder is used to produce a uniform and fine powder having an average particle diameter of 1 to 5.0 μm by a pulverization method using a jet milling technique. At this time, the process of manufacturing the alloy strip into fine powder is performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
Compacting in a magnetic field was performed using fine rare earth powder pulverized by jet milling as follows. The mold was filled with rare earth powder in a nitrogen atmosphere, and the rare earth powder was oriented in a uniaxial direction by applying a direct-current magnetic field by electromagnets positioned on the left and right of the mold, and at the same time, compression molding was performed by applying pressures of upper and lower punches, thereby producing a molded body. The molded body obtained by the press molding in the magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 c or less to completely remove the remaining impure organic materials, and the temperature is raised to 1050 c and maintained for 2 hours to perform a sintering densification process.
After the sintered body was produced by the above sintering production process, the sintered body was processed into a magnet having dimensions of 12.5mm × 12.5mm × 5mm, and then the following grain boundary diffusion process was performed to improve high-temperature magnetic characteristics.
After immersing the processed magnet in an alkaline degreasing agent solution, the processed magnet is rubbed with a ceramic ball having a diameter of 2 pi to 10 pi to remove any oil component on the surface of the magnet, and the magnet is washed clean with distilled water several times, thereby completely removing the residual degreasing agent.
In order to uniformly apply the rare earth compound to the surface of the washed processed body, Nd hydride, Ho hydride, Dy hydride, and Tb hydride compounds are respectively adjusted to a ratio of 50%: 50% with alcohol and uniformly mixed, thereby preparing a rare earth compound slurry. Then, while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the processed body was immersed therein and maintained for 1 to 2 minutes, so that the rare earth compound was uniformly coated on the surface of the magnet.
In order to diffuse the coated rare earth compound into the grain boundaries inside the magnet, the coated body was charged into a heating furnace, heated at a heating rate of 1 ℃/minute in an argon atmosphere, and held at a temperature of 900 ℃ for 6 hours, so that the rare earth compound was diffused into the magnet and subjected to a permeation reaction. After the diffusion treatment, the diffusion layer was removed from the surface, and then stress relief heat treatment was performed at a temperature of 900 ℃ for 10 hours. Further, after the diffusion treatment was completed, the diffusion treatment was performed again under the same conditions using Nd hydride, Ho hydride, Dy hydride, and Tb hydride compounds as coating materials, thereby manufacturing a final sample.
Table 1 shows the evaluation results of the magnetic properties of the magnets produced by producing a sintered body composed of 31 wt% Nd-1 wt% B-2 wt% TM-with the balance being wt% Fe (M ═ Cu, Al, Nb, Co) and then performing the first grain boundary diffusion and the second grain boundary diffusion using Nd hydride, Ho hydride, Dy hydride, and Tb hydride compounds as coating materials.
[ Table 1]
Referring to table 1, it can be confirmed that in the case of comparative example 1-1, Nd hydride was diffused only once so that the residual magnetic flux density (Br) was 13.8(kG) and the coercive force was 15.2(kOe), whereas in the case of example 1-1, Nd hydride was diffused twice so that the residual magnetic flux density (Br) had the same performance level of 13.8(kG) and the coercive force was increased to 16.4 (kOe). It was confirmed that examples 1-2 to 1-4 also had improved coercive force. That is, it was confirmed that the magnetic characteristics can be improved by repeating the diffusion process. At this time, it was confirmed that when Tb hydride was used for the diffusion twice, the coercive force was most improved.
[ example 2]
An alloy consisting of X wt% RE-Y wt% B-Z wt% TM-the balance wt% Fe (where RE ═ rare earth element, TM ═ 3d transition element, X ═ 28 to 35, Y ═ 0.5 to 1.5, and Z ═ 0 to 15) was melted in an argon atmosphere by an induction heating method, and then rapidly cooled by using a strip casting method, thereby producing an alloy strip.
In the course of coarsely pulverizing the produced alloy strip, the strip is charged into a vacuum furnace, evacuated, and then maintained in a hydrogen atmosphere for at least 2 hours so that hydrogen is absorbed into the strip. Subsequently, the strip was heated to 600 ℃ in a vacuum atmosphere, thereby removing hydrogen present in the interior of the strip. The coarsely pulverized and hydrotreated powder is used to produce a uniform and fine powder having an average particle diameter of 1 to 5.0 μm by a pulverization method using a jet milling technique. At this time, the process of manufacturing the alloy strip into fine powder is performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
The fine rare earth powder pulverized by jet milling was used for compaction in a magnetic field as follows. The mold was filled with rare earth powder in a nitrogen atmosphere, and the rare earth powder was oriented in the uniaxial direction by applying a direct-current magnetic field by electromagnets positioned on the left and right of the mold, and at the same time, compression molding was performed by applying pressures of upper and lower punches, thereby producing a molded body. The molded body obtained by the press molding in the magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 c or less to completely remove the remaining impure organic materials, and the temperature is raised to 1050 c and maintained for 2 hours to perform a sintering densification process.
After the sintered body was produced by the above sintering production process, the sintered body was processed into a magnet having dimensions of 12.5mm × 12.5mm × 5mm, and then the following grain boundary diffusion process was performed to improve high-temperature magnetic characteristics.
After immersing the processed magnet in an alkaline degreasing agent solution, the processed magnet is rubbed with ceramic balls having a size of 2 pi to 10 pi to remove any oil components on the surface of the magnet, and the magnet is washed clean with distilled water several times, thereby completely removing the residual degreasing agent.
In order to uniformly apply the rare earth compound to the surface of the washed processed body, the Nd hydride compound and the alcohol were adjusted to a ratio of 50%: 50% and uniformly mixed, thereby preparing a rare earth compound slurry. Then, while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the processed body was immersed therein and maintained for 1 to 2 minutes, so that the rare earth compound was uniformly coated on the surface of the magnet. In order to diffuse the coated rare earth compound into the grain boundaries inside the magnet, the coated body was charged into a heating furnace, heated at a heating rate of 1 ℃/minute in an argon atmosphere, and held at a temperature of 900 ℃ for 6 hours, so that the rare earth compound was diffused into the magnet and subjected to a permeation reaction. After the diffusion treatment, the diffusion layer was removed from the surface, and then stress relief heat treatment was performed at a temperature of 900 ℃ for 10 hours.
Further, after the diffusion treatment was completed, the diffusion treatment was performed again under the same conditions using Ho hydride, Dy hydride and Tb hydride compounds as coating materials, thereby manufacturing a final sample.
Table 2 shows the evaluation results of the magnetic properties of the magnets produced by producing a sintered body composed of 31 wt% Nd-1 wt% B-2 wt% TM-with the balance being wt% Fe (M ═ Cu, Al, Nb, Co), performing first grain boundary diffusion using a Nd hydride compound as a coating material, and then performing second grain boundary diffusion using a Ho hydride, Dy hydride, and Tb hydride compound.
[ Table 2]
Referring to table 2, it can be determined that in the case of comparative example 1-2, when Ho hydride is diffused only once, the remanent magnetic flux density (Br) is 13.7(kG), and the coercive force is 15.9(kOe), whereas in the case of example 2-1, Nd hydride is diffused first, and then Ho hydride is diffused second, and thus, the remanent magnetic flux density (Br) has the same performance level of 13.7(kG), and the coercive force is increased to 17.8 (kOe). Further, it was confirmed that examples 2-2 and 2-3 also have improved coercive force. That is, it was determined that the magnetic characteristics can be improved by the repeated diffusion process using different coating materials. At this time, it can be confirmed that the coercive force is significantly improved in the case of examples 2 to 3 in which Nd hydride is diffused first and then Tb hydride is diffused.
[ example 3]
An alloy consisting of X wt% RE-Y wt% B-Z wt% TM-the balance wt% Fe (where RE ═ rare earth element, TM ═ 3d transition element, X ═ 28 to 35, Y ═ 0.5 to 1.5, and Z ═ 0 to 15) was melted in an argon atmosphere by an induction heating method, and then rapidly cooled by using a strip casting method, thereby producing an alloy strip.
In the course of coarsely pulverizing the produced alloy strip, the strip is charged into a vacuum furnace, evacuated, and then maintained in a hydrogen atmosphere for at least 2 hours so that hydrogen is absorbed into the strip. Subsequently, the strip was heated to 600 ℃ in a vacuum atmosphere, thereby removing hydrogen present in the interior of the strip. The coarsely pulverized and hydrotreated powder is used to produce a uniform and fine powder having an average particle diameter of 1 to 5.0 μm by a pulverization method using a jet milling technique. At this time, the process of manufacturing the alloy strip into fine powder is performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
The fine rare earth powder pulverized by jet milling was used for compaction in a magnetic field as follows. The mold was filled with rare earth powder in a nitrogen atmosphere, and the rare earth powder was oriented in the uniaxial direction by applying a direct-current magnetic field by electromagnets positioned on the left and right of the mold, and at the same time, compression molding was performed by applying pressures of upper and lower punches, thereby producing a molded body. The molded body obtained by the press molding in the magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 c or less to completely remove the remaining impure organic materials, and the temperature is raised to 1050 c and maintained for 2 hours to perform a sintering densification process.
After the sintered body was produced by the above sintering production process, the sintered body was processed into a magnet having dimensions of 12.5mm × 12.5mm × 5mm, and then the following grain boundary diffusion process was performed to improve high-temperature magnetic characteristics. After immersing the processed magnet in an alkaline degreasing agent solution, the processed magnet is rubbed with ceramic balls having a size of 2 pi to 10 pi to remove any oil components on the surface of the magnet, and the magnet is washed clean with distilled water several times, thereby completely removing the residual degreasing agent.
In order to uniformly apply the rare earth compound to the surface of the washed processed body, Ho hydride, Dy hydride, and Tb hydride compounds are respectively adjusted to a ratio of 50%: 50% with alcohol, and uniformly mixed, thereby preparing a rare earth compound slurry. Then, while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the processed body was immersed therein and maintained for 1 to 2 minutes, so that the rare earth compound was uniformly coated on the surface of the magnet.
In order to diffuse the coated rare earth compound into the grain boundaries inside the magnet, the coated body was charged into a heating furnace, heated at a heating rate of 1 ℃/minute in an argon atmosphere, and held at a temperature of 900 ℃ for 6 hours, so that the rare earth compound was diffused into the magnet and subjected to a permeation reaction. After the diffusion treatment, the diffusion layer was removed from the surface, followed by stress relief heat treatment at a temperature of 900 ℃ for 10 hours, and then final heat treatment at a temperature of 500 ℃ for 2 hours.
Further, after the diffusion treatment was completed, the diffusion treatment was performed again under the same conditions by using Nd hydride compound as a coating material, thereby manufacturing a final sample.
Table 3 shows the evaluation results of the magnetic properties of the magnets produced by producing a sintered body composed of 31 wt% Nd-1 wt% B-2 wt% TM-with the balance being wt% Fe (M ═ Cu, Al, Nb, Co), performing first grain boundary diffusion using a Ho hydride, Dy hydride, and Tb hydride compound as coating materials, and then performing second grain boundary diffusion using a Nd hydride compound.
[ Table 3]
Referring to table 3, it can be determined that the Br reduction rate according to temperature is-0.13 (%/° c) when the Ho hydride is diffused only once and the Hcj reduction rate according to temperature is-0.65 (%/° c) in the case of comparative example 1-2, whereas the Br reduction rate according to temperature has the same performance level of-0.13 (%/° c) and the Hcj reduction rate improves to-0.55 (%/° c) when the Ho hydride is diffused first and then the Nd hydride is diffused second in the case of example 3-1. That is, it was confirmed that the magnetic characteristics can be improved using the repeated diffusion process of different coating materials.
[ example 4]
An alloy consisting of X wt% RE-Y wt% B-Z wt% TM-the balance wt% Fe (where RE ═ rare earth element, TM ═ 3d transition element, X ═ 28 to 35, Y ═ 0.5 to 1.5, and Z ═ 0 to 15) was melted in an argon atmosphere by an induction heating method, and then rapidly cooled by using a strip casting method, thereby producing an alloy strip.
In the course of coarsely pulverizing the produced alloy strip, the strip is charged into a vacuum furnace, evacuated, and then maintained in a hydrogen atmosphere for at least 2 hours so that hydrogen is absorbed into the strip. Subsequently, the strip was heated to 600 ℃ in a vacuum atmosphere, thereby removing hydrogen present in the interior of the strip. The coarsely pulverized and hydrotreated powder is used to produce a uniform and fine powder having an average particle diameter of 1 to 5.0 μm by a pulverization method using a jet milling technique. At this time, the process of manufacturing the alloy strip into fine powder is performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
The fine rare earth powder pulverized by jet milling was used for compaction in a magnetic field as follows. The mold is filled with rare earth powder in a nitrogen atmosphere, and the rare earth powder is oriented in a uniaxial direction by applying a direct-current magnetic field by electromagnets positioned at the left and right of the mold, and compression molding is performed by simultaneously applying pressures of upper and lower punches, thereby manufacturing a molded body. The molded body obtained by the press molding in the magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 c or less to completely remove the remaining impure organic materials, and the temperature is raised to 1050 c and maintained for 2 hours to perform a sintering densification process.
After the sintered body was produced by the above sintering production process, the sintered body was processed into a magnet having dimensions of 12.5mm × 12.5mm × 5mm, and then the following grain boundary diffusion process was performed to improve high-temperature magnetic characteristics. After immersing the processed magnet in an alkaline degreasing agent solution, the processed magnet is rubbed with ceramic balls having a size of 2 pi to 10 pi to remove any oil components on the surface of the magnet, and the magnet is washed clean with distilled water several times, thereby completely removing the residual degreasing agent.
In order to uniformly apply the rare earth compound to the surface of the washed processed body, the rare earth compound is prepared by mixing Ho hydride and Dy hydride powders in a weight ratio of 50%: 50%. Further, a rare earth compound obtained by mixing two different types of powders and an alcohol are adjusted to a ratio of 50%: 50% and uniformly mixed, thereby preparing a heterogeneous rare earth compound slurry. Then, while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the processed body was immersed therein and maintained for 1 to 2 minutes, so that the rare earth compound was uniformly coated on the surface of the magnet.
In order to diffuse the coated rare earth compound into the grain boundaries inside the magnet, the coated body was charged into a heating furnace, heated at a heating rate of 1 ℃/minute in an argon atmosphere, and held at a temperature of 900 ℃ for 6 hours, so that the rare earth compound was diffused into the magnet and subjected to a permeation reaction. After the diffusion treatment, the diffusion layer was removed from the surface, stress relief heat treatment was performed at a temperature of 900 ℃ for 10 hours, and then final heat treatment was performed at a temperature of 500 ℃ for 2 hours, thereby manufacturing a final sample.
Table 4 shows the evaluation results of the magnetic properties of the magnets produced by producing a sintered body composed of 31 wt% Nd-1 wt% B-2 wt% TM-the balance being wt% Fe (M ═ Cu, Al, Nb, Co), mixing a Ho hydride and a Dy hydride compound at a ratio of 50%: 50% as a coating material, and then performing grain boundary diffusion.
[ Table 4]
Referring to table 4, it can be determined that in the case of comparative examples 1 to 3, only Dy hydride was used so that the remanent flux density (Br) was 13.6(kG) and the coercive force was 21.5(kOe), whereas in the case of examples 4 to 5, the remanent flux density (Br) was 13.66(kG) and the coercive force was 19.01 (kOe). That is, it was confirmed that in the case of examples 4 to 5, using only 50% Dy hydride reduced the manufacturing cost while the performance was comparable to that in the case of using 100% Dy hydride. Further, it was confirmed that in the case of examples 4 to 14, the remanent magnetic flux density (Br) was 13.43(kG) and the coercive force was 20.01(kOe), and therefore the performance was almost equivalent to that of comparative examples 1 to 3.
[ example 5]
An alloy consisting of X wt% RE-Y wt% B-Z wt% TM-the balance wt% Fe (where RE ═ rare earth element, TM ═ 3d transition element, X ═ 28 to 35, Y ═ 0.5 to 1.5, and Z ═ 0 to 15) was melted in an argon atmosphere by an induction heating method, and then rapidly cooled by using a strip casting method, thereby producing an alloy strip.
In the course of coarsely pulverizing the produced alloy strip, the strip is charged into a vacuum furnace, evacuated, and then maintained in a hydrogen atmosphere for at least 2 hours so that hydrogen is absorbed into the strip. Subsequently, the strip was heated to 600 ℃ in a vacuum atmosphere, thereby removing hydrogen present in the interior of the strip. The coarsely pulverized and hydrotreated powder is used to produce a uniform and fine powder having an average particle diameter of 1 to 5.0 μm by a pulverization method using a jet milling technique. At this time, the process of manufacturing the alloy strip into fine powder is performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
The fine rare earth powder pulverized by jet milling was used for compaction in a magnetic field as follows. The mold was filled with rare earth powder in a nitrogen atmosphere, and the rare earth powder was oriented in the uniaxial direction by applying a direct-current magnetic field by electromagnets positioned on the left and right of the mold, and at the same time, compression molding was performed by applying pressures of upper and lower punches, thereby producing a molded body. The molded body obtained by the press molding in the magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 c or less to completely remove the remaining impure organic materials, and the temperature is raised to 1050 c and maintained for 2 hours to perform a sintering densification process.
After the sintered body was produced by the above sintering production process, the sintered body was processed into a magnet having dimensions of 12.5mm × 12.5mm × 5mm, and then the following grain boundary diffusion process was performed to improve high-temperature magnetic characteristics. After immersing the processed magnet in an alkaline degreasing agent solution, the processed magnet is rubbed with ceramic balls having a size of 2 pi to 10 pi to remove any oil components on the surface of the magnet, and the magnet is washed clean with distilled water several times, thereby completely removing the residual degreasing agent.
In order to uniformly apply the rare earth compound to the surface of the washed processed body, the rare earth compound is prepared by mixing Nd hydride and Dy hydride powders in a weight ratio of 50%: 50%. Further, a rare earth compound obtained by mixing two different types of powders and an alcohol are adjusted to a ratio of 50%: 50% and uniformly mixed, thereby preparing a heterogeneous rare earth compound slurry. While the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the processed body was immersed therein and maintained for 1 to 2 minutes so that the rare earth compound was uniformly coated on the surface of the magnet.
In order to diffuse the coated rare earth compound into the grain boundaries inside the magnet, the coated body was charged into a heating furnace, heated at a heating rate of 1 ℃/minute in an argon atmosphere, and held at a temperature of 900 ℃ for 6 hours, so that the rare earth compound was diffused into the magnet and subjected to a permeation reaction. After the diffusion treatment, the diffusion layer was removed from the surface, stress relief heat treatment was performed at a temperature of 900 ℃ for 10 hours, and then final heat treatment was performed at a temperature of 500 ℃ for 2 hours, thereby manufacturing a final sample.
Table 5 shows the evaluation results of the magnetic properties of the magnets produced by producing a sintered body composed of 31 wt% Nd-1 wt% B-2 wt% TM-the balance being wt% Fe (M ═ Cu, Al, Nb, Co), mixing Nd hydride and Dy hydride compounds at a ratio of 50%: 50% as coating materials, and then performing grain boundary diffusion.
[ Table 5]
Referring to table 5, it can be determined that in the case of comparative examples 1 to 3, only Dy hydride was used so that the remanent flux density (Br) was 13.6(kG) and the coercive force was 21.5(kOe), whereas in the case of examples 5 to 4, the remanent flux density (Br) was 13.96(kG) and the coercive force was 20.33 (kOe). That is, it was confirmed that, in the case of example 5-4, even when only 50% Dy hydride was used, the performance was comparable to that in the case where 100% Dy hydride was used. Further, it was confirmed that in the cases of examples 5 to 16, the remanent flux density (Br) was 13.98(kG) and the coercive force was 20.35(kOe), and therefore the performance was almost equivalent to that of comparative examples 1 to 3.
[ example 6]
An alloy consisting of X wt% RE-Y wt% B-Z wt% TM-the balance wt% Fe (where RE ═ rare earth element, TM ═ 3d transition element, X ═ 28 to 35, Y ═ 0.5 to 1.5, and Z ═ 0 to 15) was melted in an argon atmosphere by an induction heating method, and then rapidly cooled by using a strip casting method, thereby producing an alloy strip.
In the course of coarsely pulverizing the produced alloy strip, the strip is charged into a vacuum furnace, evacuated, and then maintained in a hydrogen atmosphere for at least 2 hours so that hydrogen is absorbed into the strip. Subsequently, the strip was heated to 600 ℃ in a vacuum atmosphere, thereby removing hydrogen present in the interior of the strip. The coarsely pulverized and hydrotreated powder is used to produce a uniform and fine powder having an average particle diameter of 1 to 5.0 μm by a pulverization method using a jet milling technique. At this time, the process of manufacturing the alloy strip into fine powder is performed in a nitrogen or inert gas atmosphere to prevent deterioration of magnetic characteristics due to contamination by oxygen.
The fine rare earth powder pulverized by jet milling was used for compaction in a magnetic field as follows. The mold was filled with rare earth powder in a nitrogen atmosphere, and the rare earth powder was oriented in the uniaxial direction by applying a direct-current magnetic field by electromagnets positioned on the left and right of the mold, and at the same time, compression molding was performed by applying pressures of upper and lower punches, thereby producing a molded body. The molded body obtained by the press molding in the magnetic field is charged into a sintering furnace and sufficiently maintained in a vacuum atmosphere and at a temperature of 400 c or less to completely remove the remaining impure organic materials, and the temperature is raised to 1050 c and maintained for 2 hours to perform a sintering densification process.
After the sintered body was produced by the above sintering production process, the sintered body was processed into a magnet having dimensions of 12.5mm × 12.5mm × 5mm, and then the following grain boundary diffusion process was performed to improve high-temperature magnetic characteristics. After immersing the processed magnet in an alkaline degreasing agent solution, the processed magnet is rubbed with ceramic balls having a size of 2 pi to 10 pi to remove any oil components on the surface of the magnet, and the magnet is washed clean with distilled water several times, thereby completely removing the residual degreasing agent.
In order to uniformly apply the rare earth compound to the surface of the washed processed body, the rare earth compound was prepared by mixing Ho hydride and Dy hydride powders in a weight ratio of 75% to 25%. Further, a rare earth compound obtained by mixing two different types of powders and an alcohol are adjusted to a ratio of 50%: 50% and uniformly mixed, thereby preparing a heterogeneous rare earth compound slurry. Then, while the prepared slurry was put into a beaker and uniformly dispersed by using an ultrasonic cleaner, the processed body was immersed therein and maintained for 1 to 2 minutes, so that the rare earth compound was uniformly coated on the surface of the magnet.
In order to diffuse the coated rare earth compound into the grain boundaries inside the magnet, the coated body was charged into a heating furnace, heated at a heating rate of 1 ℃/minute in an argon atmosphere, and held at a temperature of 900 ℃ for 6 hours, so that the rare earth compound was diffused into the magnet and subjected to a permeation reaction. After the diffusion treatment, the diffusion layer was removed from the surface, stress relief heat treatment was performed at a temperature of 900 ℃ for 10 hours, and then final heat treatment was performed at a temperature of 500 ℃ for 2 hours, thereby manufacturing a final sample.
Table 6 shows the evaluation results of the magnetic properties of the magnets produced by producing a sintered body composed of 31 wt% Nd-1 wt% B-2 wt% TM-the balance being wt% Fe (M ═ Cu, Al, Nb, Co), mixing a Ho hydride and a Dy hydride compound at a ratio of 50%: 50% as a coating material, and then performing grain boundary diffusion.
[ Table 6]
Referring to table 6, it can be confirmed that in the case of examples 6-1 to 6-6, the coercive force is lower than that of the example of table 5. That is, it was confirmed that the coercive force was not significantly improved as compared with that of example 5 because the amount of Ho hydride was three times as large as that of Dy hydride. Fig. 10 is a graph of the change in remanence (Br) according to the coating amount, and fig. 11 is a graph of the change in coercivity (Hcj) according to the coating amount.
Referring to fig. 10, when Dy hydride is mixed with Nd hydride, the remanent magnetic flux density (Br) increases in some regions, as compared to the case where Dy hydride alone is used. Further, referring to fig. 11, the coercive force (Hcj) has a similar level of performance when Dy hydride is mixed with Nd hydride, as compared with the case where Dy hydride alone is used.
Although the embodiments have been mainly described above, these are only examples and do not limit the present invention. Further, the present invention may be changed and modified in various ways by those skilled in the art without departing from the essential characteristics of the present invention. For example, the constituent elements described in detail in the embodiments of the present invention may be modified. Furthermore, differences due to modifications and application should be construed as being included in the scope and spirit of the present invention as described in the appended claims.
Claims (10)
1. A method of manufacturing a rare earth magnet, the method comprising:
preparing a magnetic sintered body containing RE, Fe and B as constituent components (RE is selected from one or two or more selected from rare earth elements);
applying a solution containing a grain boundary diffusion material to the sintered body; and
grain boundary diffusion is performed by heat-treating the sintered body,
wherein the grain boundary diffusion material comprises a Heavy Rare Earth Element (HREE) hydride and a Light Rare Earth Element (LREE) hydride.
2. The method of claim 1, wherein the Heavy Rare Earth Element (HREE) hydride comprises at least one of Dy hydride, Tb hydride, and Ho hydride.
3. The method of claim 2, wherein the Light Rare Earth Element (LREE) hydride comprises Nd hydride (NdHx).
4. The method of claim 1, wherein the amount of the Heavy Rare Earth Element (HREE) hydride is less than the amount of the Light Rare Earth Element (LREE) hydride.
5. The method of claim 4, wherein the amount of the Heavy Rare Earth Element (HREE) hydride is greater than the amount of the Light Rare Earth Element (LREE) hydride.
6. A method of manufacturing a rare earth magnet, the method comprising:
preparing a magnetic sintered body containing RE, Fe and B as constituent components (RE is selected from one or two or more selected from rare earth elements);
applying a first solution containing a first grain boundary diffusion material to the sintered body;
performing first grain boundary diffusion by heat-treating the sintered body;
applying a second solution comprising a second grain boundary diffusion material to the sintered body; and
the second grain boundary diffusion is performed by heat-treating the sintered body.
7. The method of claim 6, wherein the first grain boundary diffusion material comprises a Heavy Rare Earth Element (HREE) hydride, and
the second grain boundary diffusion material comprises a Light Rare Earth Element (LREE) hydride.
8. The method of claim 6, wherein the first grain boundary diffusion material comprises a Light Rare Earth Element (LREE) hydride, and
the second grain boundary diffusion material comprises a hydride of a Heavy Rare Earth Element (HREE).
9. The method of claim 7 or 8, wherein the Heavy Rare Earth Element (HREE) hydride comprises at least one of Dy hydride, Tb hydride, and Ho hydride, and
the Light Rare Earth Element (LREE) hydride includes Nd hydride.
10. A motor comprising a rare earth magnet manufactured by the method according to any one of claims 1 to 8.
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| Application Number | Priority Date | Filing Date | Title |
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| KR1020180148750A KR102561239B1 (en) | 2018-11-27 | 2018-11-27 | Manufacturing method of rare earth magnet |
| KR10-2018-0148750 | 2018-11-27 | ||
| PCT/KR2019/016464 WO2020111772A1 (en) | 2018-11-27 | 2019-11-27 | Method for manufacturing rare earth magnet |
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| CN113168961A true CN113168961A (en) | 2021-07-23 |
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| US (1) | US20220028609A1 (en) |
| EP (1) | EP3889979A4 (en) |
| KR (1) | KR102561239B1 (en) |
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| KR102435666B1 (en) * | 2021-12-29 | 2022-08-25 | 성림첨단산업(주) | Method for manufacturing rare earth permanent magnet and rare earth permanent magnet manufactured therefrom |
| CN114783755B (en) * | 2022-04-20 | 2024-03-05 | 杨杭福 | Method for preparing samarium-iron-nitrogen magnet by electric field thermal field co-assistance |
Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101652821A (en) * | 2007-07-02 | 2010-02-17 | 日立金属株式会社 | R-fe-B type rare earth sintered magnet and process for production of the same |
| JP2012015168A (en) * | 2010-06-29 | 2012-01-19 | Showa Denko Kk | R-t-b-based rare earth permanent magnet, motor, vehicle, generator and wind power generator |
| JP2012043968A (en) * | 2010-08-19 | 2012-03-01 | Toyota Central R&D Labs Inc | Rare earth sintered magnet and method for manufacturing the same |
| JP2013105903A (en) * | 2011-11-14 | 2013-05-30 | Toyota Motor Corp | Manufacturing method of rare earth magnet |
| US20130135069A1 (en) * | 2010-07-14 | 2013-05-30 | Noritaka Miyamoto | Permanent magnet and method of producing permanent magnet |
| JP2014150119A (en) * | 2013-01-31 | 2014-08-21 | Hitachi Metals Ltd | Method of manufacturing r-t-b based sintered magnet |
| US20150302961A1 (en) * | 2014-04-18 | 2015-10-22 | Korea University Research And Business Foundation | Fabrication method of rare earth-based sintered magnet |
| CN106298135A (en) * | 2016-08-31 | 2017-01-04 | 烟台正海磁性材料股份有限公司 | A kind of manufacture method of R Fe B class sintered magnet |
| CN106601401A (en) * | 2016-12-14 | 2017-04-26 | 中国工程物理研究院材料研究所 | Preparation method of high-abundance rare earth sintered neodymium-iron-boron magnet capable of regulating and controlling grain boundary multi-layer structure and product prepared by preparation method |
| CN107658087A (en) * | 2016-07-25 | 2018-02-02 | Tdk株式会社 | R T B systems sintered magnet |
| WO2018143229A1 (en) * | 2017-01-31 | 2018-08-09 | 日立金属株式会社 | Method for producing r-t-b sintered magnet |
| US20180286545A1 (en) * | 2017-03-30 | 2018-10-04 | Tdk Corporation | R-t-b based sintered magnet |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4831074B2 (en) * | 2006-01-31 | 2011-12-07 | 日立金属株式会社 | R-Fe-B rare earth sintered magnet and method for producing the same |
| JP5515539B2 (en) * | 2009-09-09 | 2014-06-11 | 日産自動車株式会社 | Magnet molded body and method for producing the same |
| KR101516567B1 (en) * | 2014-12-31 | 2015-05-28 | 성림첨단산업(주) | RE-Fe-B BASED RARE EARTH MAGNET BY GRAIN BOUNDARY DIFFUSION OF HAEVY RARE EARTH AND MANUFACTURING METHODS THEREOF |
| JP6760169B2 (en) * | 2017-03-27 | 2020-09-23 | 日立金属株式会社 | Manufacturing method of RTB-based sintered magnet |
| US10734143B2 (en) * | 2017-03-30 | 2020-08-04 | Tdk Corporation | R-T-B based sintered magnet |
| JP7035682B2 (en) * | 2017-03-30 | 2022-03-15 | Tdk株式会社 | RTB-based sintered magnet |
| US10748685B2 (en) * | 2017-03-30 | 2020-08-18 | Tdk Corporation | R-T-B based sintered magnet |
| KR102373412B1 (en) * | 2017-12-01 | 2022-03-14 | 현대자동차주식회사 | Method for preparing rare-earth permanent magnet |
-
2018
- 2018-11-27 KR KR1020180148750A patent/KR102561239B1/en active IP Right Grant
-
2019
- 2019-11-27 US US17/297,600 patent/US20220028609A1/en active Pending
- 2019-11-27 CN CN201980078204.8A patent/CN113168961A/en active Pending
- 2019-11-27 EP EP19891663.7A patent/EP3889979A4/en active Pending
- 2019-11-27 WO PCT/KR2019/016464 patent/WO2020111772A1/en unknown
Patent Citations (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101652821A (en) * | 2007-07-02 | 2010-02-17 | 日立金属株式会社 | R-fe-B type rare earth sintered magnet and process for production of the same |
| JP2012015168A (en) * | 2010-06-29 | 2012-01-19 | Showa Denko Kk | R-t-b-based rare earth permanent magnet, motor, vehicle, generator and wind power generator |
| US20130135069A1 (en) * | 2010-07-14 | 2013-05-30 | Noritaka Miyamoto | Permanent magnet and method of producing permanent magnet |
| JP2012043968A (en) * | 2010-08-19 | 2012-03-01 | Toyota Central R&D Labs Inc | Rare earth sintered magnet and method for manufacturing the same |
| JP2013105903A (en) * | 2011-11-14 | 2013-05-30 | Toyota Motor Corp | Manufacturing method of rare earth magnet |
| JP2014150119A (en) * | 2013-01-31 | 2014-08-21 | Hitachi Metals Ltd | Method of manufacturing r-t-b based sintered magnet |
| US20150302961A1 (en) * | 2014-04-18 | 2015-10-22 | Korea University Research And Business Foundation | Fabrication method of rare earth-based sintered magnet |
| CN107658087A (en) * | 2016-07-25 | 2018-02-02 | Tdk株式会社 | R T B systems sintered magnet |
| CN106298135A (en) * | 2016-08-31 | 2017-01-04 | 烟台正海磁性材料股份有限公司 | A kind of manufacture method of R Fe B class sintered magnet |
| CN106601401A (en) * | 2016-12-14 | 2017-04-26 | 中国工程物理研究院材料研究所 | Preparation method of high-abundance rare earth sintered neodymium-iron-boron magnet capable of regulating and controlling grain boundary multi-layer structure and product prepared by preparation method |
| WO2018143229A1 (en) * | 2017-01-31 | 2018-08-09 | 日立金属株式会社 | Method for producing r-t-b sintered magnet |
| US20180286545A1 (en) * | 2017-03-30 | 2018-10-04 | Tdk Corporation | R-t-b based sintered magnet |
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| KR20200062849A (en) | 2020-06-04 |
| EP3889979A1 (en) | 2021-10-06 |
| WO2020111772A1 (en) | 2020-06-04 |
| EP3889979A4 (en) | 2022-08-24 |
| US20220028609A1 (en) | 2022-01-27 |
| KR102561239B1 (en) | 2023-07-31 |
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